WO2020111570A1 - Tôle d'acier électrique non orientée présentant des propriétés magnétiques supérieures et procédé de production de celle-ci - Google Patents

Tôle d'acier électrique non orientée présentant des propriétés magnétiques supérieures et procédé de production de celle-ci Download PDF

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WO2020111570A1
WO2020111570A1 PCT/KR2019/015193 KR2019015193W WO2020111570A1 WO 2020111570 A1 WO2020111570 A1 WO 2020111570A1 KR 2019015193 W KR2019015193 W KR 2019015193W WO 2020111570 A1 WO2020111570 A1 WO 2020111570A1
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steel sheet
oriented electrical
electrical steel
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PCT/KR2019/015193
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English (en)
Korean (ko)
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이헌주
김용수
신수용
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주식회사 포스코
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Priority to US17/298,129 priority Critical patent/US20220018002A1/en
Priority to EP19888950.3A priority patent/EP3889284A1/fr
Priority to CN201980079240.6A priority patent/CN113166881A/zh
Priority to JP2021531070A priority patent/JP7253054B2/ja
Publication of WO2020111570A1 publication Critical patent/WO2020111570A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1233—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2202/00—Physical properties
    • C22C2202/02—Magnetic

Definitions

  • the present invention relates to a non-oriented electrical steel sheet and a method for manufacturing the same. More specifically, the present invention relates to a non-oriented electrical steel sheet used as an iron core material for a rotating device such as a motor and a generator, and a method for manufacturing the same.
  • the non-oriented electrical steel sheet is mainly used for a motor that converts electrical energy into mechanical energy, and requires excellent magnetic properties of the non-oriented electrical steel sheet to exhibit high efficiency in the process.
  • eco-friendly technology has attracted attention, it is considered very important to increase the efficiency of a motor, which accounts for the majority of the total electric energy consumption, thereby increasing the demand for non-oriented electrical steel sheets having excellent magnetic properties.
  • the magnetic properties of non-oriented electrical steel sheet are mainly evaluated by iron loss and magnetic flux density.
  • Iron loss refers to energy loss generated at a specific magnetic flux density and frequency
  • magnetic flux density refers to the degree of magnetization obtained under a specific magnetic field. The lower the iron loss, the more energy-efficient the motor can be manufactured under the same conditions, and the higher the magnetic flux density, the smaller the motor or the smaller the copper loss, making a non-oriented electrical steel sheet with low iron loss and high magnetic flux density. It is important.
  • the characteristics of the non-oriented electrical steel sheet to be considered also change.
  • many motors consider the iron loss W 15/50 most importantly when a 1.5T magnetic field is applied at a commercial frequency of 50Hz.
  • W 15/50 iron loss is not all motors for various applications, and may evaluate the iron loss at different frequencies or applied magnetic fields depending on the main operating conditions.
  • non-oriented electrical steel sheet having a thickness of 0.35 mm or less which is used in recent electric vehicle driving motors
  • magnetic properties are often important at low magnetic fields of 1.0 T or less and high frequencies of 400 Hz or more, so iron loss such as W 10/400 As a result, the properties of the non-oriented electrical steel sheet are evaluated.
  • a method commonly used to increase the magnetic properties of non-oriented electrical steel sheets is to add alloy elements such as Si.
  • the specific resistivity of the steel can be increased through the addition of these alloying elements.
  • the eddy current loss decreases, thereby reducing the total iron loss.
  • the amount of Si added increases, the magnetic flux density becomes inferior and the brittleness increases, and if it is added over a certain amount, cold rolling is impossible and commercial production becomes impossible.
  • the maximum content of Si available for commercial production is known to be about 3.5 to 4.0%, and by adding elements such as Al and Mn to increase the resistivity of additional steel, it is possible to produce the highest quality non-oriented electrical steel sheet with excellent magnetic properties.
  • Separation of iron loss can be classified into three types: hysteresis loss, classical eddy current loss, and abnormal eddy current loss.
  • hysteresis loss the effect obtained by increasing the specific resistance of the steel is a decrease in eddy current loss, and it is known that when the specific resistance increases to 65 ⁇ cm or more, the effect of reducing iron loss is significantly reduced. Therefore, it is important to reduce the hysteresis loss in order to reduce the iron loss in the high resistivity component system.
  • a method of reducing hysteresis loss there are a method of suppressing the influence of precipitates and non-metallic inclusions that may interfere with the movement of a magnetic wall, a method of reducing residual stress, or a method of developing an aggregate structure favorable to magnetism.
  • a method of reducing iron loss of a non-oriented electrical steel sheet by controlling precipitates or non-metallic inclusions has been continuously developed.
  • one of the other prior arts is a technique of obtaining a low iron loss by controlling the composition of an inclusion formed from a composite oxide of Si, Al, and Mn in addition to a low Al content.
  • the present invention is to provide a non-oriented electrical steel sheet and its manufacturing method. More specifically, the present invention relates to a non-oriented electrical steel sheet used as an iron core material for a rotating device such as a motor and a generator, and a method of manufacturing the same.
  • Non-oriented electrical steel sheet according to an embodiment of the present invention, by weight, Si: 2.5 to 3.8%, Al: 0.5 to 2.5%, Mn: 0.2 to 4.5%, C: 0.005% or less (excluding 0%) ), S: 0.005% or less (excluding 0%), N: 0.005% or less (excluding 0%), Nb: 0.004% or less (excluding 0%), Ti: 0.004% or less (0% Excluded), V: 0.004% or less (excluding 0%), Ta: 0.0005 to 0.0025%, balance Fe and unavoidable impurities.
  • the steel sheet includes at least one of carbide-based precipitates, nitride-based precipitates, or sulfide-based precipitates having a diameter of 20 to 100 nm, and the distribution density of each of carbide-based precipitates, nitride-based precipitates, and sulfide-based precipitates is 0.9/ ⁇ m 2 or less Can be. More specifically, the distribution density may be 0.5 pieces/ ⁇ m 2 or less.
  • the thickness of the steel sheet may be 0.1 to 0.3 mm.
  • the average grain size of the steel sheet may be 40 to 100 ⁇ m.
  • the hysteresis loss is less than 1.0W / kg in W 15/50 core loss, the hysteresis loss can be less than 3.8W / kg in core loss W 10/400.
  • the manufacturing method of the non-oriented electrical steel sheet according to an embodiment of the present invention by weight, Si: 2.5 to 3.8%, Al: 0.5 to 2.5%, Mn: 0.2 to 4.5%, C: 0.005% or less ( 0% excluded), S: 0.005% or less (excluding 0%), N: 0.005% or less (excluding 0%), Nb: 0.004% or less (excluding 0%), Ti: 0.004% Or less (excluding 0%), V: 0.004% or less (excluding 0%), Ta: 0.0005 to 0.0025%, preparing a slab containing residual Fe and unavoidable impurities; Heating the slab; Hot-rolling the heated slab to produce a hot-rolled sheet; Cold rolling the hot rolled sheet to produce a cold rolled sheet; And manufacturing an electric steel sheet by final annealing the cold rolled sheet.
  • the steel sheet includes at least one of carbide-based precipitates, nitride-based precipitates, or sulfide-based precipitates having a diameter of 20 to 100 nm, and the distribution density of each of carbide-based precipitates, nitride-based precipitates, or sulfide-based precipitates is 0.9/ ⁇ m 2 or less Can be. More specifically, the distribution density may be 0.5 pieces/ ⁇ m 2 or less.
  • One embodiment of the present invention by limiting the Si, Al, Mn content to have a sufficiently high specific resistance, while limiting the C, N, S, Nb, Ti, V content while presenting the optimum content range of Ta, the magnetic By suppressing the formation of carbide-based precipitates, nitride-based precipitates, or sulfide-based precipitates having a diameter of 20 to 100 nm, it is possible to provide a non-oriented electrical steel sheet excellent in magnetism with low hysteresis loss.
  • first, second, and third are used to describe various parts, components, regions, layers, and/or sections, but are not limited thereto. These terms are only used to distinguish one part, component, region, layer or section from another part, component, region, layer or section. Accordingly, a first portion, component, region, layer or section described below may be referred to as a second portion, component, region, layer or section without departing from the scope of the present invention.
  • the term "combination of these" included in the expression of the marki form means one or more mixtures or combinations selected from the group consisting of the elements described in the expression of the marki form, the components It means to include one or more selected from the group consisting of.
  • a part when it is said that a part is “on” or “on” another part, it may be directly on or on another part, or another part may be involved therebetween. In contrast, if one part is referred to as being “just above” another part, no other part is interposed therebetween.
  • % means weight%, and 1 ppm is 0.0001% by weight.
  • the meaning of further including an additional element means that the remaining amount of iron (Fe) is replaced by an additional amount of the additional element.
  • carbide-based precipitates, nitride-based precipitates, or sulfide-based precipitates having a diameter of 20 to 100 nm interfere with magnetic wall movement and deteriorate magnetic properties of the electrical steel sheet.
  • Ta an appropriate amount of Ta in addition to the various components contained in the steel, it is possible to suppress the formation of precipitates having a diameter of 20 to 100 nm. Therefore, it should be noted that as a result, a non-oriented electrical steel sheet having excellent magnetic properties can be produced.
  • the non-oriented electrical steel sheet according to an embodiment of the present invention in weight%, Si: 2.5 to 3.8%, Al: 0.5 to 2.5%, Mn: 0.2 to 4.5%, C: 0.005% or less (excluding 0%) S), S: 0.005% or less (excluding 0%), N: 0.005% or less (excluding 0%), Nb: 0.004% or less (excluding 0%), Ti: 0.004% or less (0%) Excluding), V: 0.004% or less (excluding 0%), Ta: 0.0005 to 0.0025%, balance Fe and unavoidable impurities.
  • Cu 0.025% or less (excluding 0%)
  • B 0.002% or less (excluding 0%)
  • Mg 0.005% or less (excluding 0%)
  • Zr 0.005% or less ( (Excluding 0%)).
  • the steel sheet includes at least one of carbide-based precipitates, nitride-based precipitates, or sulfide-based precipitates having a diameter of 20 to 100 nm, and the distribution density of each of carbide-based precipitates, nitride-based precipitates, and sulfide-based precipitates is 0.9. Dogs/ ⁇ m 2 or less. More specifically, the distribution density may be 0.5 pieces/ ⁇ m 2 or less.
  • Si serves to lower the iron loss by increasing the specific resistance of the material, and if added too little, the effect of improving the high-frequency iron loss may be insufficient. Conversely, if too much is added, the brittleness of the material increases, and the cold rolling property is extremely deteriorated, so that productivity and punchability may drop sharply. Therefore, Si can be added in the aforementioned range. More specifically, it may contain 2.7 to 3.7% by weight of Si. More specifically, it may contain 3.0 to 3.6% by weight of Si.
  • Al serves to lower the iron loss by increasing the specific resistance of the material, and if it is added too little, it may be difficult to obtain a magnetic improvement effect by forming a fine nitride. Conversely, if too much is added, the nitride is excessively formed, thereby deteriorating the magnetic properties, and problems in all processes such as steelmaking and continuous casting can be caused, thereby significantly degrading productivity. Therefore, Al can be added in the above-mentioned range. More specifically, it may contain 0.5 to 2.3% by weight of Al. More specifically, it may contain 0.7 to 2.0% by weight of Al.
  • Mn increases the specific resistance of the material, thereby improving iron loss and forming sulfides. When too little is added, sulfides are formed finely and may cause magnetic deterioration. Conversely, if too much is added, MnS is excessively precipitated, and the magnetic flux density can be drastically decreased by promoting the formation of ⁇ 111 ⁇ aggregates that are unfavorable to magnetism. Therefore, Mn can be added in the above-mentioned range. More specifically, Mn may include 0.3 to 4.0% by weight. More specifically, Mn may include 0.7 to 2.0% by weight.
  • C causes self-aging and combines with other impurity elements to produce carbides, thereby lowering the magnetic properties, so the lower is preferable, and more specifically, it can be managed at 0.003% by weight or less.
  • N 0.005% by weight or less (excluding 0%)
  • N not only forms fine and long AlN precipitates inside the base material, but also combines with other impurities to form fine nitrides, thereby inhibiting grain growth and deteriorating iron loss. Can be.
  • MnS and CuS are formed to deteriorate magnetic properties and deteriorate hot workability, so it is better to manage low, but is an element indispensable in steel, and more specifically, it should be managed at 0.003% by weight or less.
  • Nb, Ti, and V are elements with a very strong tendency to form precipitates in the steel, and deteriorate iron loss by inhibiting grain growth by forming fine carbide or nitride or sulfide inside the base material.
  • carbon, vaginal, and sulfide-based precipitates containing Nb, Ti, and V having a diameter of 20 to 100 nm greatly degrade magnetic properties, and when Nb, Ti, and V contents exceed 0.004% by weight, precipitates with a diameter of 20 to 100 nm are formed. This is encouraged. Therefore, the Nb, Ti, and V content should be managed at 0.004% or less, and more specifically 0.002% or less.
  • the diameter of the precipitate means a diameter of the circle in an imaginary circle having the same area as the area occupied by the precipitate.
  • Ta 0.0005 to 0.0025% by weight
  • Ta is known as an element that forms carbides when added in a small amount in the steel, and generally forms a complex carbide together with Nb, Ti, and V.
  • the Ta content in the steel is 0.0005 to 0.0025% by weight, there is an effect of coarsening the size of the carbide to 100 nm or more, thereby suppressing the formation of carbides having a diameter of 20 to 100 nm harmful to magnetism. In addition, it suppresses the formation of nitrides and sulfides of 20 to 100 nm in size. If the Ta content is too large, the fraction of precipitates having a size of 20 to 100 nm increases, which is harmful to magnetism. On the contrary, if too small, the inhibitory effect of 20 to 100 nm does not appear.
  • impurities such as Cu, B, Mg, and Zr, which are inevitably incorporated, may be included. These elements are trace amounts, but may cause magnetic deterioration through the formation of inclusions in the steel, etc., so that Cu: 0.025% by weight or less (excluding 0%), B: 0.002% by weight or less (excluding 0%), Mg: 0.005 It should be controlled to less than weight percent (excluding 0%) and Zr: 0.005 weight percent or less (excluding 0%).
  • the present invention includes Fe and unavoidable impurities. Unavoidable impurities are widely known in the art, so a detailed description is omitted. In one embodiment of the present invention, addition of effective ingredients other than the above ingredients is not excluded.
  • the thickness of the steel sheet may be 0.1 to 0.3mm.
  • the average grain size may be 40 to 100 ⁇ m.
  • the hysteresis loss is less than 1.0W / kg in W 15/50 core loss, the hysteresis loss in the iron loss W 10/400 be not more than 3.8W / kg. More specifically, the hysteresis loss at W 15/50 iron loss may be 1.0 W/kg or less, and the hysteresis loss at W 10/400 iron loss may be 3.8 W/kg or less.
  • the magnetic flux density (B 50 ) is 1.63T or more at a thickness of 0.1 ⁇ m, 1.65T or more at a thickness of 0.15mm, 1.67T or more at 0.25mm, 1.67T at 0.27mm Above, it may be 1.68T or more at 0.30mm.
  • the magnetic flux density is a value that decreases as the thickness becomes thinner. When the magnetic flux density is high, the torque is excellent when starting and accelerating when used as an automobile motor.
  • Method of manufacturing a non-oriented electrical steel sheet according to an embodiment of the present invention is by weight, Si: 2.5 to 3.8%, Al: 0.5 to 2.5%, Mn: 0.2 to 4.5%, C: 0.005% or less (0% Excluded), S: 0.005% or less (excluding 0%), N: 0.005% or less (excluding 0%), Nb: 0.004% or less (excluding 0%), Ti: 0.004% or less (0 % Is excluded), V: 0.004% or less (excluding 0%), Ta: 0.0005 to 0.0025%, preparing a slab containing residual Fe and unavoidable impurities; Heating the slab; Hot-rolling the heated slab to produce a hot-rolled sheet; Cold rolling the hot rolled sheet to produce a cold rolled sheet; And manufacturing an electric steel sheet by final annealing the cold rolled sheet.
  • the slab Cu 0.025% or less (excluding 0%), B: 0.002% or less (excluding 0%), Mg: 0.005% or less (excluding 0%) and Zr: 0.005% or less (Excluding 0%) may further include one or more.
  • the steel sheet includes at least one of carbide-based precipitates, nitride-based precipitates, or sulfide-based precipitates having a diameter of 20 to 100 nm, and the distribution density of each of carbide-based precipitates, nitride-based precipitates, or sulfide-based precipitates is 0.9. / ⁇ m 2 or less. More specifically, the distribution density may be 0.5 pieces/ ⁇ m 2 or less.
  • manufacturing a hot rolled sheet; Thereafter, annealing the hot-rolled sheet may be further included.
  • a slab satisfying the above-described composition is prepared.
  • the reason for limiting the addition ratio of each composition in the slab is the same as the reason for limiting the composition of the non-oriented electrical steel sheet described above, and thus repeated description will be omitted. Since the composition of the slab is not substantially changed in the manufacturing process of hot rolling, hot rolled sheet annealing, cold rolling, final annealing, which will be described later, the composition of the slab and the composition of the non-oriented electrical steel sheet are substantially the same.
  • the prepared slab is heated.
  • the subsequent hot rolling process can be performed smoothly, and the slab can be homogenized. More specifically, heating may mean reheating.
  • the slab heating temperature may be 1100 to 1250 °C. If the heating temperature of the slab is too high, precipitates may be redissolved and finely precipitated after hot rolling.
  • hot-rolled slabs are produced by hot rolling the slabs.
  • the finish rolling temperature of hot rolling may be 750°C or higher.
  • the method may further include annealing the hot rolled sheet.
  • the hot-rolled sheet annealing temperature may be 850 to 1150°C.
  • the temperature range may be 950 to 1125°C.
  • the annealing temperature of the hot rolled sheet may be 900 to 1100°C. The hot-rolled sheet annealing is performed to increase the orientation favorable to magnetism as necessary, and may be omitted.
  • the hot rolled sheet is pickled and cold rolled to a predetermined plate thickness to produce a cold rolled sheet. It may be applied differently depending on the thickness of the hot-rolled sheet, but a reduction rate of 70 to 95% may be applied, and cold-rolled sheet may be manufactured by cold rolling to a final thickness of 0.1 to 0.6 mm. More specifically, a cold rolled sheet may be manufactured by cold rolling so that the final thickness is 0.1 to 0.3 mm.
  • an electric steel sheet is manufactured by final annealing the cold rolled sheet.
  • the final annealing temperature can be 800 to 1050°C. If the final annealing temperature is too low, recrystallization does not occur sufficiently, and if the final annealing temperature is too high, rapid growth of crystal grains may occur, resulting in magnetic flux density and high-frequency iron loss. More specifically, final annealing may be performed at a temperature of 900 to 1000°C. In the final annealing process, all the processed tissues formed in the cold rolling step (ie, 99% or more) may be recrystallized.
  • a steel ingot was prepared by vacuum dissolving in the laboratory and using the components shown in Table 1. This was reheated to 1150°C and hot-rolled to a finish temperature of 780°C to produce a hot-rolled sheet with a plate thickness of 2.0mm.
  • the hot-rolled hot-rolled sheet was annealed at 1030°C for 100 seconds, followed by pickling and cold rolling to obtain a thickness of 0.15, 0.25, 0.27, 0.30 mm, and recrystallization annealing at 1000°C for 110 seconds.
  • carbides, nitrides, and sulfides all mean precipitates having a diameter of 20 to 100 nm. Magnetic properties such as magnetic flux density and iron loss were averaged by measuring the width of 60 mm ⁇ length of 60 mm ⁇ 5 sheets of specimens for each specimen and measuring them in the rolling direction and the rolling vertical direction with a single sheet tester.
  • W 10/400 is the core loss at the time when the magnetic flux density in the organic 1.0T at a frequency of 400Hz
  • W 10/50 of iron loss is when the magnetic flux density of 1.0T in the organic frequency of 50Hz
  • B 50 is It means the magnetic flux density induced in the magnetic field of 5000A/m.
  • W h 15/50 and W h 10/400 are 60 mm wide ⁇ 60 mm long ⁇ 5 specimens for each specimen, and the DC magnetic meter measures the amount of energy lost at 1.5T and 1.0T in mJ/kg. Measured by and multiplied by the frequency of 50Hz and 400Hz, respectively, and the average of 5 measurements was obtained. At this time, the measurement speed was 50 mT/s.
  • A3, A4, B3, B4, C3, C4, D3, D4, E3, E4 with appropriately controlled alloy components have a 20 to 100 nm diameter carbide, nitride, and sulfide distribution density of 0.9 Since it was good at less than dog/ ⁇ m 2 , all of the magnetic properties were excellent.
  • A1 and A2 had a large amount of C, so the distribution density of carbides of a size harmful to magnetism increased, resulting in poor iron loss due to increased hysteresis loss and poor magnetic flux density.
  • B1, B2 is S content
  • C1, C2 is N content exceeds the range of the present invention, respectively, the distribution density of sulfide and nitride of a size harmful to magnetism is increased, so iron loss and magnetic flux density are inferior.
  • D1, D2, and E1 respectively, because Nb, Ti, and V exceeded the scope of the present invention, and the distribution density of carbides having a size harmful to magnetism increased by more than 0.9/ ⁇ m 2 , iron loss and magnetic flux density were inferior.
  • E2 has an inferior iron loss and magnetic flux density due to an increase in the distribution of carbides of a size harmful to magnetism because the Ta content is outside the scope of the present invention.

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Abstract

La présente invention concerne une tôle d'acier électrique non orientée ayant des propriétés magnétiques esupérieure et un procédé de production de celle-ci. La tôle d'acier électrique non orientée selon un mode de réalisation de la présente invention comprend, en % en poids, Si: 2,5-3,8%, Al: 0,5 à -2,5%, Mn: 0,2 À 4,5%, C: 0,005% ou moins, S: 0,005% ou moins, N: 0,005 % ou moins (à l'exclusion de 0%), Nb: 0,004% ou moins, et Ti: 0,004% ou moins (à l'exclusion de 0%), V: 0,004 % ou moins (à l'exclusion de 0%), Ta: 0,0005-0,0025%, le reste étant du Fe et les impuretés inévitables.
PCT/KR2019/015193 2018-11-30 2019-11-08 Tôle d'acier électrique non orientée présentant des propriétés magnétiques supérieures et procédé de production de celle-ci WO2020111570A1 (fr)

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US17/298,129 US20220018002A1 (en) 2018-11-30 2019-11-08 Non-oriented electrical steel sheet having superior magnetic properties and method of manufacturing same
EP19888950.3A EP3889284A1 (fr) 2018-11-30 2019-11-08 Tôle d'acier électrique non orientée présentant des propriétés magnétiques supérieures et procédé de production de celle-ci
CN201980079240.6A CN113166881A (zh) 2018-11-30 2019-11-08 磁性优异的无取向电工钢板及其制造方法
JP2021531070A JP7253054B2 (ja) 2018-11-30 2019-11-08 磁性に優れる無方向性電磁鋼板およびその製造方法

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